Yttrium α-Sialon Ceramics by Hot Isostatic Pressing and Post-Hot Isostatic Pressing

Authors

  • Alena Bartek,

    1. AB Sandvik Hard Materials, S-126 80 Stockholm, Sweden; Department of Engineering Materials, Luleå University of Technology, S-951 87 Luleå, Sweden; School of Materials Science and Engineering, University of New South Wales, Kensington, NSW 2033, Australia
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    • *

      Member, American Ceramic Society.

  • Thommy Ekström,

    1. AB Sandvik Hard Materials, S-126 80 Stockholm, Sweden; Department of Engineering Materials, Luleå University of Technology, S-951 87 Luleå, Sweden; School of Materials Science and Engineering, University of New South Wales, Kensington, NSW 2033, Australia
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    • Lulcå University of Tehnology.

    • AB Sandvik Hard Materials.

  • Harald Herbertsson,

    1. AB Sandvik Hard Materials, S-126 80 Stockholm, Sweden; Department of Engineering Materials, Luleå University of Technology, S-951 87 Luleå, Sweden; School of Materials Science and Engineering, University of New South Wales, Kensington, NSW 2033, Australia
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    • Lulcå University of Tehnology.

    • University of New South Wales.

  • Thomas Johansson

    1. AB Sandvik Hard Materials, S-126 80 Stockholm, Sweden; Department of Engineering Materials, Luleå University of Technology, S-951 87 Luleå, Sweden; School of Materials Science and Engineering, University of New South Wales, Kensington, NSW 2033, Australia
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    • Lulcå University of Tehnology.


  • J. Smialek-contributing editor

  • Supported by the Swedish Board for Technical Development and the Norrland Foundation.

Abstract

Dense α-sialon materials were produced by hot isostatic pressing (HIP) and post-hot isostatic pressing (post-HIP) using compositions with the formula Yx(Si12–4.5x, Al4.5x)-(O1.5x,N16–1.5x) with 0.1 ≤x≤ 0.9 and with the same compositions with extra additions of yttria and aluminum nitride. X-ray diffraction analyses show how the phase content changes from large amounts of β-sialon (x= 0.1) to large amounts of α-sialon (x= 0.4) and increasing amounts of mellilite and sialon polytypoids (x= 0.8). Samples HIPed at 1600°C for 2 h contained unreacted α-silicon nitride, while those HIPed at 1750°C for 1 h did not. This could be due to the fact that the time is to short to achieve equilibrium or that the high pressure (200 MPa) prohibits α-sialon formation. Sintering at atmospheric pressure leads to open porosity for all compositions except those with excess yttria. Therefore, only samples with excess yttria were post-HIPed. Microstructrual analyses showed that the post-HIPed samples had the highest α-sialon content. A higher amount of α-sialon and subsequently a lower amount of intergranular phase were detected at x= 0.3 and x= 0.4 in the post-HIPed samples in comparison to the HIPed. The hardness (HV10) and fracture toughness (KIC) did not differ significantly between HIPed and post-HIPed materials but vary with different x values due to different phase contents. Measurements of cell parameters for all compositions show a continuous increase with increasing x value which is enhanced by high pressure at high x values.

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